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Synthesis of Core@shell Structured CuFeS2@TiO<sub>2</sub> Magnetic Nanomaterial and Its Application for Hydrogen Production by Methanol Aqueous Solution Photosplitting
Synthesis of Core@shell Structured CuFeS2@TiO2 Magnetic Nanomaterial and Its Application for Hydrogen Production by Methanol Aqueous Solution Photosplitting
Bulletin of the Korean Chemical Society. 2014. Sep, 35(9): 2813-2817
Copyright © 2014, Korea Chemical Society
  • Received : April 10, 2014
  • Accepted : May 29, 2014
  • Published : September 20, 2014
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About the Authors
Sora Kang
Byeong Sub Kwak
Minkyu Park
Kyung Mi Jeong
Department of Engineering in Energy and Applied Chemistry, Silla University, Busan 617-736, Korea
Sun-Min Park
Korean Institutes of Ceramic Engineering and Technology (KICET), Seoul 153-801, Korea
Misook Kang

Abstract
A new magnetic semiconductor material was synthesized to enable separation after a liquid-type photocatalysis process. Core@shell-structured CuFeS 2 @TiO 2 magnetic nanoparticles were prepared by a combination of solvothermal and wet-impregnation methods for photocatalysis applications. The materials obtained were characterized using X-ray diffraction, transmission electron microscopy, ultraviolet-visible, photoluminescence spectroscopy, Brunauer-Emmett-Teller surface area measurements, and cyclic voltammetry. This study confirmed that the light absorption of CuFeS 2 was shifted significantly to the visible wavelength compared to pure TiO 2 . Moreover, the resulting hydrogen production from the photo-splitting methanol/water solution after 10 hours was more than 4 times on the core@shell structured CuFeS 2 @TiO 2 nanocatalyst than on either pure TiO 2 or CuFeS 2 .
Keywords
Introduction
The use of hydrogen as an energy source is expected increase because of its environmentally friendly nature. Of the methods for generating hydrogen, the photocatalytic splitting of water using TiO 2 1,2 and MTiO 3 3,4 semiconductors has attracted considerable attention. The principle of photocatalytic water splitting is based on the conversion of light energy to electricity upon the exposure of a semiconductor to light. Upon exposure to incident light, the electrons of n -type semiconducting materials are emitted from the conduction band to the valence bands, leading to the holes in valence bands. These electrons and holes split water molecules into oxygen and hydrogen. 5 The band gap required for hydrogen production by water splitting need to be at least 1.2 eV. Pure TiO 2 and various MTiO 3 photocatalysts (where M = a metal) have band gaps of 3.0-5.0 eV, making them ineffective in this reaction. In addition, hydrogen production is limited by the rapid recombination of holes and electrons. 6 To overcome this rapid recombination, considerable efforts have been made to increase hydrogen evolution using methanol, ethanol, or a mixture of light alcohol and water, rather than water because lower energies of approximately 0.6-0.8 eV are needed. 7,8
One issue in a liquid photocatalytic reaction is how to recover the catalyst from a liquid solution after the reaction. This paper introduces a core@shell multi-component catalyst, which has attracted considerable attention recently because of its potential applications in electronics, magnetism, optics, and catalysis. 9-13 The magnetic core used can be collected conveniently and separated using a magnet. Therefore, magnetic-based TiO 2 photocatalyst synthesis will be very useful. On the other hand, it is difficult to produce TiO 2 -coated particles with UV or visible-light photoactivity without sacrificing the magnetic properties. Some studies evaluated the use of magnetite (Fe 3 O 4 ) cores. 14-17 Recently, more stable transition-metal incorporated MFe 2 O 4 (M = Ni, Co, Fe, Sr) super-paramagnetic materials have been used as core materials and have produced good results for the photocatalytic destruction of organic compounds. 18-21 On the other hand, oxygenated cores are difficult to activate under visible-light, so materials containing sulfur or nitrogen are used. Therefore, the perfect core@shell structured MFeS 2 @TiO 2 magnetic photocatalysts require further development. Furthermore, higher photocatalytic activity can be expected when a metal with higher reduction potentials, Cu or Ag, is inserted into MFeS 2 core, but comparatively little developmental work has been conducted on redox applications.
The major objective of this study was to develop core@shell-structured CuFeS 2 @TiO 2 photocatalysts with improved catalytic properties for the production of hydrogen from methanol/water aqueous systems, and with magnetic properties commensurate with the separations. The nature of the CuFeS 2 @TiO 2 photocatalyst produced were examined by X-ray diffraction (XRD), UV-visible spectroscopy, photoluminescence (PL) spectroscopy, Brunauer-Emmett-Teller (BET) surface area measurements, and magnetic momentum using a vibrating sample magnetometer.
Experimental
Core@shell structured CuFeS 2 @TiO 2 was prepared using sequential solvothermal and impregnation hybrid methods, as shown in Figure 1 . In step 1 of a), to prepare the CuFeS 2 sol mixture, iron chloride (FeCl 3 ·6H 2 O, 99.95%, Junsei Chemical, Japan) and cupper chloride (CuCl·5H 2 O, 99.95%, Junsei Chemical, Japan) were used as the Fe and Cu precursors, respectively, and ethanol was used as the solvent. Briefly, 0.04 mol of FeCl 3 and 0.04 mol of CuCl 2 were added to 400 mL of ethanol, and stirred for 1 h.
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Synthetic sequence for the TiO2, CuFeS2, and CuFeS2@ TiO2 photocatalyst.
Thioacetamide (C 2 H 5 NS) was added to the upper solution as a sulfur source. Thioacetamide is used widely in classical qualitative inorganic analysis as an in situ source of sulfide ions. Therefore, the treatment of aqueous solutions of many metal cations to a solution of thioacetamide affords the corresponding metal sulfide:
  • M++M3++ 2CH3C(S)NH2+ H2O→ MMS2+ 2CH3C(O)NH2+ 4 H+
In the next step, ethylenediamine was added to reduce Fe 3+ to Fe 2.5+ . The final solution was stirred until it became homogeneous, and was then treated thermally in an autoclave at 200 ℃ for 2 h. After the thermal treatment, the obtained powder was cooled, washed with ethanol, and dried at 80 ℃ for 24 h. Here, pure TiO 2 was also synthesized using a solvothermal method, which is the same process (b) to CuFeS 2 . 22 Titanium tetraisopropoxide (TTIP, Junsei Chemical, Japan) was used as the Ti precursor. The solution in the synthesis step was fixed to pH = 3, and the thermal treatment was performed in an autoclave at 200 ℃ for 8 h. In step 3 of c), the magnetic CuFeS 2 particles were coated with TiO 2 . The CuFeS 2 and TiO 2 with a 1.0 molar ratio were added to 100 mL of ethanol and its pH was fixed to 5 by HCl. The resulting colloid was stirred for 3 h. After stirring the solution until it became homogeneous, the colloid was evaporated at 70 ℃ for 3 h. The resulting precipitate was heated to 200 ℃ for 2 h under argon to remove the solvent and generate an anatase shell.
The TiO 2 , CuFeS 2 , and CuFeS 2 @TiO 2 (analyzed as approximately CuFeS 2 :TiO 2 = 1:1) powders were examined by XRD (X'Pert Pro MPD PANalytical 2-circle diffractometer) using nickel-filtered CuKα radiation (30 kV, 30 mA) at 2θ angles from 5 to 70°, a scan speed of 10° min –1 , and a time constant of 1 s. The sizes and shapes of the TiO 2 , CuFeS 2 , and 1CuFeS 2 @1TiO 2 particles were determined by transmission electron microscopy (TEM, JEOL 2000EX) at 200 kV. The specific surface area and pore size distribution were calculated according to the BET theory, which gives the isotherm equation for multilayer adsorption by the generalization of Langmuir’s treatment of a multi-molecular layer. The adsorptiondesorption isotherm analysis to identify the BET surface area and pore size distribution of particles was performed using a Belsorp II instrument. All the particles were degassed under vacuum at 150 ℃ for 2 h before the measurements, and measured by nitrogen gas adsorption using a continuous flow method with a mixture of nitrogen and helium as the carrier gas. The UV-visible spectra of the TiO 2 , CuFeS 2 , and 1CuFeS 2 @1TiO 2 powders were obtained using a Shimadzu MPS-2000 spectrometer (Kyoto, Japan) equipped with a reflectance sphere over the range, 200 to 800 nm. The magnetic properties were measured using a vibrating sample magnetometer (VSM) on a physical property measurement system (Quantum Design PPMS-9). Photoluminescence (PL) spectroscopy was carried out on the three powders to examine photo-excited electron hole pairs using 1.0 mm thick pellets of TiO 2 , CuFeS 2 , and 1CuFeS 2 @1TiO 2 at room temperature using a He-Cd laser source at a wavelength of 325 nm.
The photosplitting of methanol/water was performed using a liquid photo reactor designed in this laboratory. 23 To photosplit methanol/water (1:1 vol./vol., total volume = 1.0 L) solution, 0.5 g of powdered TiO 2 , CuFeS 2 , and 1CuFeS 2 @1TiO 2 photocatalysts were added to 1.0 L of a methanol/water solution in a 2.0-L Pyrex reactor. UV-lamps (6 × 3 Wcm −2 = 18 Wcm −2 , 30 cm length × 2.0 cm diameter; Shinan, Korea) emitting at 365 nm were used. The photosplitting of methanol/water was carried out over 1-8 h with stirring, and hydrogen evolution was measured after 1 h of operation. The hydrogen gas (H 2 ) produced during methanol/water photosplitting was analyzed by TCD-type gas chromatography (GC; model DS 6200; Donam Instruments Inc., Korea). To identify the products and intermediates, GC was connected directly to a photo-reactor. The following GC conditions were used: TCD detector; Carbosphere column (Alltech, Deerfield, IL, USA); injection temperature 140 ℃; initial temperature 120 ℃; final temperature 120 ℃; and detector temperature 150 ℃.
Results and Discussion
Figure 2(a) and (b) shows XRD patterns and TEM images of the TiO 2 , CuFeS 2 , and 1CuFeS 2 @1TiO 2 powders. First in A), TiO 2 particles had a pure anatase structure with peaks at 25.3, 38.0, 48.2, 54, 63, and 68° 2θ, which were assigned to the (101), (004), (200), (105), (211), and (204) planes, respectively. 24 CuFeS 2 showed several peaks at 2θ values of 29.45 (d 112 ), 34.19° (d 200 ), 48.93° (d 220 ), 57.95° (d 321 ), 71.40° (d 400 ), 79.07° (d 332 ), and 90.99° (d 415 ), indicating a tetragonal crystal system (I-42d). 25 1CuFeS 2 @1TiO2 showed a mixed peaks of CuFeS 2 and TiO 2 , indicating the exposed CuFeS 2 or partially-covered TiO 2 on the surfaces of CuFeS 2 particles. On the other hand, peak broadening indicates a reduction in the crystallite size. 26 The Debye-Scherrer’s equation, t = 0.9λ/βcosθ (where λ is the wavelength of incident X-rays, β is the full width at half maximum height in radians, and the θ is the diffraction angle) was used to determine the crystallite size. 27 The calculated values at the representative 101 and 112 planes of TiO 2 and CuFeS 2 were 7.3 nm and 38.38 nm, respectively. The TEM images in Figure 2(b) showed slightly distorted tetragonal CuFeS 2 particles, 20 nm in size. The 1CuFeS 2 @1TiO 2 particles were partially covered by 5- 10 nm TiO 2 particles, and the particle size increased to 100 nm after core@shell formation compared to the size of pure CuFeS 2 .
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XRD patterns (a) and TEM photographs (b) of synthesized TiO2, CuFeS2, and CuFeS2@TiO2 powders.
Figure 3 shows the adsorption-desorption isotherm curves of N 2 at 77 K for the TiO 2 , CuFeS 2 , and 1CuFeS 2 @1TiO 2 powders. The isotherms of TiO 2 and 1CuFeS 2 @1TiO 2 belonged to IV type in the IUPAC classification 28 ; this hysteresis slope has been observed in the presence of mesopores. The mesopores are considered to be bulk pores formed between the TiO 2 particles. Otherwise, the isotherms of CuFeS 2 mean non-pores with an III type. This suggests that a high surface area facilitates adsorption, which can generate adsorption activity. Therefore, some molecules are adsorbed more easily on the surfaces of the TiO 2 and core@shell structured 1CuS@1TiO 2 than CuFeS 2 . On the other hand, the surface area, pore volume, and pore size are listed in the table below. The specific surface areas of TiO 2 and 1CuFeS 2 @1TiO 2 were large, 154.21 and 73.70 m 2 g −1 , respectively. On the other hand, it decreased in CuFeS 2 to 24.50 m 2 g −1 . Here, the specific surface area in this study might depend on the bulk pores formed by aggregation between the TiO 2 particles in the shell, and the pore volumes showed the same tendency to the surface areas.
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Adsorption-desorption isotherm curves of N2 at 77 K for the TiO2, CuFeS2, and 1CuFeS2@1TiO2 powders.
The UV-visible diffuse reflectance (a) and PL spectra (b) of TiO 2 and CuFeS 2 powders were also obtained ( Figure 4 ). The absorption band corresponding to the octahedral symmetry of Ti 4+ was observed at ~350 to 380 nm, indicating a bandgap of 2.90 eV. 29 Generally, the band gaps of semiconductor materials are closely related to the absorption wavelength, where a higher wavelength indicates a smaller band gap. CuFeS 2 exhibited a continuous absorption band in the range 200-700 nm, which concurs with its black color. Using Tauc’s equation, 30 its band-gap was estimated to be approximately 0.75 eV. Figure 4(b) presents the photoluminescence (PL) spectra of TiO 2 , CuFeS 2 , and 1CuFeS 2 @1TiO 2 pellets. The PL emission spectra are useful for examining the efficiency of the charge transfer behavior of photo-generated electrons and holes. The PL curves show that the electrons in the valence band are transferred to the conduction band, and then return to the valence band by photoemission. In general, the PL intensity increases with increasing number of photons emitted as a result of the recombination of electrons and holes, resulting in a decrease in photoactivity. 31 Therefore, there is a strong relationship between the PL intensity and photoactivity. The PL spectrum of 1CuFeS 2 @1TiO 2 showed that the PL intensity of TiO 2 was quenched substantially by the CuFeS 2 magnetic core. The CuFeS 2 in 1CuFeS 2 @1TiO 2 captures photo-generated electrons from the TiO 2 conduction band, in particular Cu ions, which separates the photogenerated electron-hole pairs. The presence of Cu in the CuFeS 2 magnetic core reduces the recombination rate, and reduces the PL spectrum intensity, indicating that the PL intensity depends on electron capture by Cu ions.
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UV-visible diffuse reflectance spectra (a) and photoluminescence (PL) (b) spectra of TiO2, CuFeS2, and CuFeS2@TiO2 powders.
Figure 5 shows the saturation magnetization (emu/g) versus coercivity (Hc) plots obtained at room temperature for CuFeS 2 and CuFeS 2 @TiO 2 , and the inset shows an enlarged figure at an almost zero applied magnetic field. The two samples have hysteresis cycles that are characteristic of ferromagnetism. The saturation magnetizations of CuFeS 2 and CuFeS 2 @TiO 2 were similar but the value of CuFeS 2 was approximately two times larger than that of CuFeS 2 @TiO 2 . This suggests that the TiO 2 shell was responsible for the observed reduction in ferromagnetism. The TiO 2 anatase structure is diamagnetic. 32,33 Occasionally, some Ti 4+ ions become Ti 3+ ions if defects are present in the TiO 2 structure, resulting in the detection of weak ferromagnetism. 34 Therefore, the ferromagnetic effect of TiO 2 depends on the method of synthesis, due to the presence of defects, particularly oxygen vacancies in TiO 2 nanomaterials. In addition, an advantage of CuFeS 2 @TiO 2 is that it can be recovered by a magnet after the reaction.
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Saturation magnetization (M) versus coercivity (Hc) plots obtained at room temperature for CuFeS2 and CuFeS2@ TiO2.
The CV results for TiO 2 and CuFeS 2 ( Figure 6 ) were strongly dependent on the analytical conditions used, and a semiconductor needs to be redox active within the experimental potential window. In this study, the potentials were measured in distilled water using a pelletized sample as the working electrode, Ag/AgCl as the reference electrode, and 0.1 M KCl as the supporting electrolyte. A reversible wave was observed, which gives the following information: reversible reactions display a hysteresis of the absolute potential between the reduction (E pc ) and oxidation (E pa ) peaks. Reversible reactions show the ratios of the peak voltages under reduction and oxidation conditions that are near unity (1 = E pa /E pc ). When such reversible peaks are observed, the thermodynamic information in the form of half-cell potentials, E 0 1/2 (E pc + E pa /2) can be determined. In particular, when the waves are semi-reversible, such as when E pa /E pc is 1, it is possible to obtain more information on the kinetic processes. A useful equation has been reported, 35 which can determine the energy levels of the highest occupied molecular orbital (HOMO) and the lowest unoccupied molecular orbital (LUMO) using CV. First, the ferrocene (E 1/2 vs. Ag/ Ag + = +0.42 eV) potential (a standard) should be measured in an electrolyte solution using the same reference electrode with −4.8 eV fixed as an energy level. Finally, the HOMO and LUMO energy levels can be calculated using the following formula: HOMO(or LUMO) (eV) = −4.8 − (E onset − E 1/2 (Ferrocene)). Here, E onset is the starting point of the redox potential, and is used more than peak potential values. The onset potentials for reduction with an Ag/AgCl reference electrode for TiO 2 and CuFeS 2 were −0.605 and 0.616 V respectively. The calculated LUMO energy levels for TiO 2 and CuFeS 2 were −3.775 and −4.996 eV respectively. This was attributed to TiO 2 electrons in the valence bands absorbing solar radiation and being excited to the conduction band. These excited electrons then move in the conduction bands to CuFeS 2 . CuFeS 2 @TiO 2 exhibited more oxidation-reduction behavior than pure TiO 2 or CuFeS 2 . Therefore, the relaxation of excited electrons is difficult, which reduces hole/electron recombination.
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CV curves of TiO2 and CuFeS2 powders.
The evolutions of H 2 from the photo-splitting of methanol/ water over TiO 2 , CuFeS 2 , and CuFeS 2 @TiO 2 powders at various molar ratios were measured in a batch-type liquid photo system and are presented in Figure 7 . No H 2 was collected from the photodecomposition of methanol/water over pure anatase CuFeS 2 after 10 h, whereas 1.80 mmol of H 2 was collected over 1CuFeS 2 @0.05TiO 2 . This was attributed to excited electron capture by the CuFeS 2 core and a reduced recombination rate. Otherwise, evolved oxygen and carbon dioxide gases could not be observed because they were partially transformed into some by-products, such as formaldehyde, acetaldehyde, formic acid, and acetic acid, by oxidation reactions with methanol molecules. On the other hand, the expected mechanism of charge separation and the photocatalytic process of CuFeS 2 and TiO 2 are shown in the adjoining diagram based on the UV-visible and CV spectra results. The conduction band position in the CuFeS 2 core is at a lower energy than that in the TiO 2 shell. Therefore, the core could act as a sink for photo-generated electrons. Under UV-light irradiation, the excited electrons from the valence band of the TiO 2 shell move into its conduction band and flowed to the surface of the shell, and they fell into the conduction band of the CuFeS 2 magnetic core. XPS confirmed that the Cu ions in CuFeS 2 were reduced after the photoreaction, meaning that the core attracts electrons during the photoreaction. Therefore, Cu + ions (3d 9 ) can accept electrons, and the electrons that move from the TiO 2 shell into CuFeS 2 core can be located in the 3d orbital of Cu ions.
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Evolution of H2 from the photo-splitting of methanol/water over TiO2, CuFeS2 and CuFeS2@TiO2 powders along with the expected mechanism of charge separation and the photocatalytic process of CuFeS2@TiO2.
Conclusion
Core@shell-structured CuFeS 2 @TiO 2 was synthesized for the production of H 2 gas from the photodecomposition of methanol/water in a batch-type liquid photo system. The core@shell morphology of synthesized CuFeS 2 @TiO 2 was examined by XRD and TEM. The PL intensity of CuFeS 2 @ TiO 2 , indicating electron/hole recombination, decreased. The ferromagnetic property of CuFeS 2 was decreased slightly by the presence of a TiO 2 shell. Hydrogen production from methanol/water was remarkably higher for 1CuFeS 2 @ 0.05TiO 2 than for pure TiO 2 , and 1.80 mmol of H 2 was collected after 10 h when 0.5 gL −1 of the powder was used. These results suggest that hydrogen production by methanol/ water splitting can be achieved more readily over the CuFeS 2 @TiO 2 magnetic material. The significant enhancement in photoactivity for methanol/water mixture splitting was attributed to the synergism between CuFeS 2 and TiO 2 , i.e ., to effective charge transfer from TiO 2 to CuFeS 2 and the suppression of electron/hole pair recombination.
Acknowledgements
This study was supported by the National Research Foundation of Korea grant funded by the Korea government (MEST) (No. 2012R1A1A3005043), for which the authors are very grateful.
References
Lin Y. C. , Liu S. H. , Syu H. R. , Ho T. H. 2012 Spectrochim. Acta A Mol. Biomol. Spectrosc. 95 300 -    DOI : 10.1016/j.saa.2012.03.080
Liu S. H. , Syu H. R. 2012 Appl. Energ. 100 148 -    DOI : 10.1016/j.apenergy.2012.03.063
Khemthong P. , Photai P. , Grisdanurak N. 2013 Int. J. Hydrogen Energy 38 15992 -    DOI : 10.1016/j.ijhydene.2013.10.065
Jin Z. , Zhang X. , Li Y. , Li S. , Lu G. 2007 Catal. Commun. 8 1267 -    DOI : 10.1016/j.catcom.2006.11.019
Zoua Z. , Ye J. , Arakawa H. 2003 Int. J. Hydrogen Energy 28 663 -    DOI : 10.1016/S0360-3199(02)00159-3
Mizoguchi H. , Ueda K. , Orita M. , Moon S. C. , Kajihara K. , Hirano M. , Hosono H. 2002 Mater. Res. Bull. 37 2401 -    DOI : 10.1016/S0025-5408(02)00974-1
Kandiel T. A. , Dillert R. , Robben L. , Bahnemann D. W. 2011 Catal. Today 161 196 -    DOI : 10.1016/j.cattod.2010.08.012
Ruiza S. O. , Zanella R. , Lópezb R. , Gordillo A. H. , Gómez R. 2013 J. Hazard. Mater. 263 2 -    DOI : 10.1016/j.jhazmat.2013.03.057
Fu W. , Yang H. , Li M. , Chang L. , Yu Q. , Xu J. , Zou G. 2006 Mater. Lett. 60 2723 -    DOI : 10.1016/j.matlet.2006.01.078
Li C. J. , Wang J. N. , Wang B. , Gong J. R. , Lin Z. 2012 Mater. Res. Bull. 47 333 -    DOI : 10.1016/j.materresbull.2011.11.012
Wilson A. , Mishra S. R. , Gupta R. , Ghosh K. 2012 J. Magn. Magn. Mater. 324 2597 -    DOI : 10.1016/j.jmmm.2012.02.009
Liang H. , Niu H. , Li P. , Tao Z. , Mao C. , Song J. , Zhang S. 2013 Mater. Res. Bull. 48 2415 -    DOI : 10.1016/j.materresbull.2013.02.066
Amarjargal A. , Tijing L. D. , Im I. T. , Kim C. S. 2013 Chem. Eng. J. 226 243 -    DOI : 10.1016/j.cej.2013.04.054
Xin T. , Ma M. , Zhang H. , Gu J. , Wang S. , Liu M. , Zhang Q. 2014 Appl. Surf. Sci. 288 51 -    DOI : 10.1016/j.apsusc.2013.09.108
Wu S. H. , Wu J. L. , Jia S. Y. , Chang Q. W. , Ren H. T. , Liu Y. 2013 Appl. Surf. Sci. 287 389 -    DOI : 10.1016/j.apsusc.2013.09.164
Chi Y. , Yuan Q. , Li Y. , Zhao L. , Li N. , Li X. , Yand W. 2013 J. Hazard. Mater. 262 404 -    DOI : 10.1016/j.jhazmat.2013.08.077
Ma P. , Jiang W. , Wang F. , Li F. , Shen P. , Chen M. , Wang Y. , Liu J. , Li P. 2013 J. Alloys Compd. 578 501 -    DOI : 10.1016/j.jallcom.2013.07.026
Mohapatra S. , Rout S. R. , Panda A. B. 2011 Colloids Surf., A: Physicochem. Eng. Aspects 384 453 -    DOI : 10.1016/j.colsurfa.2011.05.001
Wang L. , Li J. , Wang Y. , Zhao L. , Jiang Q. 2012 Chem. Eng. J. 181-182 72 -    DOI : 10.1016/j.cej.2011.10.088
Goyal A. , Bansal S. , Singha S. 2014 Int. J. Hydrogen Energy 39 4895 -    DOI : 10.1016/j.ijhydene.2014.01.050
Xiong P. , Fu Y. , Wang L. , Wang X. 2012 Chem. Eng. J. 195-196 149 -    DOI : 10.1016/j.cej.2012.05.007
Lee Y. , Chae J. , Kang M. 2010 J. Ind. Eng. Chem. 16 609 -    DOI : 10.1016/j.jiec.2010.03.008
Lee Y. , Chae J. , Kang M. 2010 J. Ind. Eng. Chem. 16 609 -    DOI : 10.1016/j.jiec.2010.03.008
Lee G. , Kang M. 2013 Curr. Appl. Phys. 13 1482 -    DOI : 10.1016/j.cap.2013.05.002
Wang Y. H. A. , Bao N. , Gupta A. 2010 Solid State Sci. 12 387 -    DOI : 10.1016/j.solidstatesciences.2009.11.019
Liu H. , Wang M. , Wang Y. , Liang Y. , Cao W. , Su Y. 2011 J. Photochem. Photobiol., A: Chem. 223 157 -    DOI : 10.1016/j.jphotochem.2011.06.014
Leong K. H. , Monash P. , Ibrahim S. , Saravanan P. 2014 Sol. Energy 101 321 -    DOI : 10.1016/j.solener.2014.01.006
Rashad M. M. , Elsayed E. M. , Al-Kotb M. S. , Shalan A. E. 2013 J. Alloys Compd. 581 71 -    DOI : 10.1016/j.jallcom.2013.07.041
Kim J. , Kang M. 2012 Int. J. Hydrogen Energy 37 8249 -    DOI : 10.1016/j.ijhydene.2012.02.057
Dua J. , Chen H. , Yang H. , Sang R. , Qian Y. , Li Y. , Zhu G. , Mao Y. , He W. , Kang D. J. 2013 Microporous Mesoporous Mater. 182 87 -    DOI : 10.1016/j.micromeso.2013.08.023
Zhang W. , Zhao J. , Liu Z. , Liu Z. , Fu Z. 2010 Appl. Surf. Sci. 256 4423 -    DOI : 10.1016/j.apsusc.2009.12.064
Lyubutin I. S. , Lin C. R. , Starchikov S. S. , Siao Y. J. , Shaikh M. O. , Funtov K. O. , Wang S. C. 2013 Acta Mater. 61 3956 -    DOI : 10.1016/j.actamat.2013.03.009
Fan L. , Dongmei J. , Yan L. , Xueming M. 2008 Phys. B: Condens. Matter. 403 2193 -    DOI : 10.1016/j.physb.2007.11.014
Wang Q. , Wei X. , Dai J. , Jiang J. , Huo X. 2014 Mater. Sci. Semicond. Process. 21 111 -    DOI : 10.1016/j.mssp.2014.01.004
Kim Y. , Jeong J. H. , Kang M. 2011 Inorg. Chim. Acta 365 400 -    DOI : 10.1016/j.ica.2010.09.041